Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
  • C22F1/18—High-melting or refractory metals or alloys based thereon
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
  • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
  • B21J1/003—Selecting material
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
  • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
  • B21J1/02—Preliminary treatment of metal stock without particular shaping, e.g. salvaging segregated zones, forging or pressing in the rough
  • B21J1/025—Preliminary treatment of metal stock without particular shaping, e.g. salvaging segregated zones, forging or pressing in the rough affecting grain orientation
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
  • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
  • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C14/00—Alloys based on titanium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
  • C22F1/18—High-melting or refractory metals or alloys based thereon
  • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon

Definitions

• the present disclosure is directed to forging methods for titanium and titanium alloys and to apparatus for conducting such methods.
• Methods for producing titanium and titanium alloys having coarse grain (CG), fine grain (FG), very fine grain (VFG), or ultrafine grain (UFG) microstructure involve the use of multiple reheats and forging steps.
• Forging steps may include one or more upset forging steps in addition to draw forging on an open die press.
• the term "coarse grain” refers to alpha grain sizes of 400 pm to greater than about 14 pm; the term “fine grain” refers to alpha grain sizes in the range of 14 pm to greater than 10 pm; the term “very fine grain” refers to alpha grain sizes of 10 pm to greater than 4.0 pm; and the term “ultra fine grain” refers to alpha grain sizes of 4.0 pm or less.
• VFG ultra fine grain
• UFG ultra fine grain
• MAF multi-axis forging
• the key to grain refinement in the ultra-slow strain rate MAF process is the ability to continually operate in a regime of dynamic recrystallization that is a result of the ultra-slow strain rates used, i.e., 0.001 s "1 or slower.
• the ultra- slow strain rate MAF process uses dynamic recrystallization to continually recrystallize grains during the forging process.
• the workpiece is then multi-axis forged.
• Multi-axis forging comprises press forging the workpiece at the workpiece forging temperature in the direction of a first orthogonal axis of the workpiece with a strain rate sufficient to adiabatically heat an internal region of the workpiece.
• Forging in the direction of the first orthogonal axis is followed by allowing the adiabatically heated internal region of the workpiece to cool to the workpiece forging temperature, while heating an outer surface region of the workpiece to the workpiece forging temperature.
• the workpiece is then press-forged at the workpiece forging temperature in the direction of a second orthogonal axis of the workpiece with a strain rate that is sufficient to adiabatically heat the internal region of the workpiece.
• Forging in the direction of the second orthogonal axis is followed by allowing the adiabatically heated internal region of the workpiece to cool to the workpiece forging temperature, while heating an outer surface region of the workpiece to the workpiece forging temperature.
• the workpiece is then press-forged at the workpiece forging temperature in the direction of a third orthogonal axis of the workpiece with a strain rate that is sufficient to adiabatically heat the internal region of the workpiece.
• Forging in the direction of the third orthogonal axis is followed by allowing the adiabatically heated internal region of the workpiece to cool to the workpiece forging temperature, while heating an outer surface region of the PATENT
• a strain rate used during press forging is in the range of 0.2 s '1 to 0.8 s '1 , inclusive.
• the workpiece comprises a cylindrical-like shape and a starting cross-sectional dimension.
• the workpiece is upset forged at the workpiece forging temperature.
• the workpiece is multiple pass draw forged at the workpiece forging temperature.
• Multiple pass draw forging comprises incrementally rotating the workpiece in a rotational direction followed by draw forging the workpiece after each rotation.
• a strain rate used in upset forging and draw forging is the range of 0.001 s "1 to 0.02 s "1 , inclusive
• the workpiece is forged at the workpiece forging temperature at a strain rate sufficient to adiabatically heat an internal region of the workpiece.
• the internal region of the workpiece is allowed to cool to the workpiece forging temperature, while an outer surface region of the workpiece is heated to the workpiece forging
• FIG. 1 is a flow chart listing steps of a non-limiting embodiment of a method according to the present disclosure for processing titanium and titanium alloys for grain size refinement;
• FIG. 2 is a schematic representation of a non-limiting embodiment of a high strain rate multi-axis forging method using thermal management for processing titanium and titanium alloys for the refinement of grain sizes, wherein FIGS. 2(a), 2(c), and 2(e) represent non-limiting press forging steps, and FIGS. 2(b), 2(d), and 2(f) represent non-limiting cooling and heating steps according to non-limiting aspects of this disclosure;
• FIG. 3 is a schematic representation of a slow strain rate multi-axis forging technique known to be used to refine grains of small scale samples
• FIG . 4 is a schematic representation of a temperature-time
• thermomechanical process chart for a non-limiting embodiment of a high strain rate multi-axis forging method according to the present disclosure
• FIG . 5 is a schematic representation of temperature-time
• thermomechanical process chart for a non-limiting embodiment of a multi-temperature high strain rate multi-axis forging method according to the present disclosure
• FIG. 6 is a schematic representation of temperature-time
• thermomechanical process chart for a non-limiting embodiment of a through beta transus high strain rate multi-axis forging method according the present disclosure
• FIG. 7 is a schematic representation of a non-limiting embodiment of a multiple upset and draw method for grain size refinement according to the present disclosure
• FIG. 8 is a flow chart listing steps of a non-limiting embodiment of a method according to the present disclosure for multiple upset and draw processing titanium and titanium alloys to refine grain size;
• FIG. 9 is a temperature-time thermomechanical chart for the non-limiting embodiment of Example 1 of this disclosure.
• FIG. 10 is a micrograph of the beta annealed material of Example 1 showing equiaxed grains with grain sizes between 10-30 pm;
• FIG. 1 1 is a micrograph of a center region of the a-b-c forged sample of Example 1 ;
• FIG. 12 a finite element modeling prediction of internal region cooling times according to a non-limiting embodiment of this disclosure
• FIG. 13 is a micrograph of the center of a cube after processing according to the embodiment of the non-limiting method described in Example 4;
• FIG. 14 is a photograph of a cross-section of a cube processed according to Example 4.
• FIG. 15 represents the results of finite element modeling to simulate deformation in thermally managed multi-axis forging of a cube processed according to Example 6;
• FIG. 16(a) is a micrograph of a cross-section from the center of the sample processed according to Example 7;
• FIG. 16(b) is a cross-section from the near surface of the sample processed according to Example 7;
• FIG. 1 7 is a schematic thermomechanical temperature-time chart of the process used in Example 9;
• FIG. 18 is a macro-photograph of a cross-section of a sample
• FIG. 19 is a micrograph of a sample processed according to the non- limiting embodiment of Example 9 showing the very fine grain size.
• FIG. 20 represents a finite element modeling simulation of deformation of the sample prepared in the non-limiting embodiment of Example 9.
• An aspect of this disclosure includes non-limiting embodiments of a multi-axis forging process that includes using high strain rates during the forging steps to refine grain size in titanium and titanium alloys. These method embodiments are PATENT
• Multi-axis forging also known as "a-b-c" forging, which is a form of severe plastic deformation, includes heating (step 22 in FIG. 1 ) a workpiece comprising a metallic material selected from titanium and a titanium alloy 24 to a workpiece forging temperature within an alpha+beta phase field of the metallic material, followed by MAF 26 using a high strain rate.
• a high strain rate is used in high strain rate MAF to adiabatically heat an internal region of the workpiece.
• the temperature of the internal region of the titanium or titanium alloy workpiece 24 should not exceed the beta- transus temperature (Tp) of the titanium or titanium alloy workpiece. Therefore, the workpiece forging temperature for at least the final a-b-c- sequence of high strain rate MAF hits should be chosen to ensure that the temperature of the internal region of the workpiece during high strain rate MAF does not equal or exceed the beta-transus temperature of the metallic material.
• the internal region temperature of the workpiece does not exceed 20°F (1 1 .1 °C) below the beta transus temperature of the metallic material, i.e., ⁇ ⁇ - 20°C (T p -1 1 .1 °C), during at least the final high strain rate sequence of a-b-c MAF hits.
• a workpiece forging temperature comprises a temperature within a workpiece forging temperature range.
• the workpiece forging temperature is in a workpiece forging temperature range of 100°F (55.6°C) below the beta transus temperature (T p ) of titanium or titanium alloy metallic material to 700°F (388.9°C) below the beta transus temperature of the titanium or titanium alloy metallic material.
• the workpiece forging PATENT is in a workpiece forging temperature range of 100°F (55.6°C) below the beta transus temperature (T p ) of titanium or titanium alloy metallic material to 700°F (388.9°C) below the beta transus temperature of the titanium or titanium alloy metallic material.
• Attorney Docket No. TAV-2139/2144/2174 temperature is in a temperature range of 300°F (166.7°C) below the beta transition temperature of titanium or the titanium alloy to 625°F (347°C) below the beta transition temperature of the titanium or titanium alloy.
• the low end of a workpiece forging temperature range is a temperature in the alpha+beta phase field wherein substantial damage does not occur to the surface of the workpiece during the forging hit, as would be known to a person having ordinary skill in the art.
• the workpiece forging temperature range when applying the embodiment of the present disclosure of FIG. 1 to a Ti-6-4 alloy (Ti-6AI-4V; UNS No. R56400), which has a beta transus temperature (T p ) of about 1850°F (1010°C), may be from 1 150°F (621 .1 °C) to 1750°F (954.4°C), or in another embodiment may be from 1225°F (662.8°C) to 1550°F (843.3°C).
• Beta annealing comprises heating the workpiece 24 above the beta transus temperature of the titanium or titanium alloy metallic material and holding for a time sufficient to form all beta phase in the workpiece. Beta annealing is a well know process and, therefore, is not described in further detail herein.
• a non-limiting embodiment of beta annealing may include heating the workpiece 24 to a beta soaking temperature of about 50°F (27.8°C) above the beta transus temperature of the titanium or titanium alloy and holding the workpiece 24 at the temperature for about 1 hour.
• MAF 26 comprises press forging (step 28, and shown in FIG. 2(a)) the workpiece 24 at the workpiece forging temperature in the direction (A) of a first orthogonal axis 30 of the workpiece using a strain rate that is sufficient to adiabatically heat the workpiece, or at least adiabatically heat an internal region of the workpiece, and plastically deform the workpiece 24.
• the phrase "internal region" as used herein refers to an PATENT
• High strain rates and fast ram speeds are used to adiabatically heat the internal region of the workpiece in non-limiting embodiments of high strain rate MAF according to this disclosure.
• the term “high strain rate” refers to a strain rate range of about 0.2 s "1 to about 0.8 s "1 , inclusive.
• the term “high strain rate” as used herein refers to a strain rate of about 0.2 s "1 to about 0.4 s "1 , inclusive.
• the internal region of the titanium or titanium alloy workpiece may be adiabatically heated to about 200°F above the workpiece forging temperature.
• the internal region is adiabatically heated to about 100°F (55.6°C) to 300°F (166.7°C) above the workpiece forging temperature.
• the internal region is adiabatically heated to about 150°F (83.3°C) to 250°F (138.9°C) above the workpiece forging temperature.
• no portion of the workpiece should be heated above the beta-transus temperature of the titanium or titanium alloy during the last sequence of high strain rate a-b-c MAF hits.
• the titanium alloy workpiece 24 is plastically deformed to a 20% to 50% reduction in height or another dimension.
• the titanium alloy workpiece 24 is plastically deformed to a 30% to 40% reduction in height or another dimension.
• a known slow strain rate multi-axis forging process is depicted schematically in FIG. 3.
• an aspect of multi-axis forging is that after every three strokes or "hits" of the forging apparatus, such as an open die forge, the shape of the workpiece approaches that of the workpiece just prior to the first hit. For example, after a 5-inch sided cubic workpiece is initially forged with a first "hit” in the direction of the "a" axis, rotated 90° and forged with a second hit in the direction of the "b" axis, and PATENT
• a first press forging step 28, shown in FIG. 2(a), also referred to herein as the "first hit”, may include press forging the workpiece on a top face down to a predetermined spacer height while the workpiece is at a workpiece forging temperature.
• a predetermined spacer height of a non-limiting embodiment is, for example, 5 inches.
• Other spacer heights, such as, for example, less than 5 inches, about 3 inches, greater than 5 inches, or 5 inches up to 30 inches are within the scope of embodiments herein, but should not be considered as limiting the scope of the present disclosure. Larger spacer heights are only limited by the capabilities of the forge and, as will be seen herein, the capabilities of the thermal management system according to the present disclosure.
• Spacer heights of less than 3 inches are also within the scope of the embodiments disclosed herein, and such relatively small spacer heights are only limited by the desired characteristics of a finished product and, possibly, any prohibitive economics that may apply to employing the present method on workpieces having relatively small sizes.
• the use of spacers of about 30 inches, for example, provides the ability to prepare billet-sized 30-inch sided cubes with fine grain size, very fine grain size, or ultrafine grain size.
• Billet-sized cubic forms of conventional alloys have been employed in forging houses for manufacturing disk, ring, and case parts for aeronautical or land-based turbines.
• a non-limiting embodiment of a method according to the present disclosure further comprises allowing (step 32) the temperature of the adiabatically heated internal region (not shown) of the workpiece to cool to the workpiece forging temperature, which is shown in FIG. 2(b).
• Internal region cooling times, or waiting times may range, for example in non-limiting embodiments, from 5 seconds to 120 seconds, from 10 seconds to 60 seconds, or from 5 seconds to 5 minutes. It will be recognized by a person skilled in the art that internal region cooling times required to cool the internal region to the workpiece forging temperature will be PATENT
• thermo management system 33 to heat the outer surface region of the workpiece to the workpiece forging temperature, together with allowing the adiabatically heated internal region to cool to the workpiece forging temperature, a non-limiting embodiment according to this disclosure may be referred to as "thermally managed, high strain rate multi-axis forging” or for purposes herein, simply as “high strain rate multi-axis forging”.
• the phrase "outer surface region” refers to a volume of about 50%, or about 60%, or about 70%, or about 80% of the cube, in the outer region of the cube
• heating 34 an outer surface region 36 of the workpiece 24 may be accomplished using one or more outer surface heating mechanisms 38 of the thermal management system 33.
• outer surface heating mechanisms 38 include, but are not limited to, flame heaters for flame PATENT
• an outer surface region heating mechanism 38 may comprise a box furnace (not shown).
• a box furnace may be configured with various heating mechanisms to heat the outer surface region of the workpiece using one or more of flame heating mechanisms, radiant heating
• the temperature of the outer surface region 36 of the workpiece 24 may be heated 34 and maintained at or near the workpiece forging temperature and within the workpiece forging temperature range using one or more die heaters 40 of a thermal management system 33.
• Die heaters 40 may be used to maintain the dies 40 or the die press forging surfaces 44 of the dies at or near the workpiece forging temperature or at temperatures within the workpiece temperature forging range.
• the dies 40 of the thermal management system are heated to a temperature within a range that includes the workpiece forging temperature up to 100°F (55.6°C) below the workpiece forging temperature.
• Die heaters 40 may heat the dies 42 or the die press forging surface 44 by any suitable heating mechanism known now or hereinafter by a person skilled in the art, including, but not limited to, flame heating mechanisms, radiant heating
• a die heater 40 may be a component of a box furnace (not shown). While the thermal management system 33 is shown in place and being used during the cooling steps 32,52,60 of the multi-axis forging process 26 shown in FIGS. 2(b), (d), and (f), it is recognized that the thermal management system 33 may or may not be in place during the press forging steps 28,46,56 depicted in FIGS. 2(a), (c), and (e). PATENT
• the workpiece 24 is plastically deformed to a plastic deformation of a 30% to 40% reduction in height or another dimension.
• the workpiece 24 may be press forged (46) in the direction of the second orthogonal axis 48 to the same spacer height used in the first press forging step (28).
• the internal region (not shown) of the workpiece 24 is adiabatically heated during the press forging step (46) to the same temperature as in the first press forging step (28).
• the high strain rates used for press forging (46) are in the same strain rate ranges as disclosed for the first press forging step (28).
• the workpiece 24 may be rotated 50 to a different orthogonal axis between successive press forging steps (e.g., 28,46).
• This rotation may be referred to as "a-b-c" rotation.
• it may be possible to rotate the ram on the forge instead of rotating the workpiece 24, or a forge may be equipped with multi-axis rams so that rotation of neither the workpiece nor the forge is required.
• the important aspect is the relative movement of the ram and the workpiece, and that rotating 50 the workpiece 24 may be an optional step. In most current industrial equipment set-ups, however, rotating 50 the workpiece to a different orthogonal axis in between press forging steps will be required to complete the multi- axis forging process 26.
• the workpiece 24 may be rotated manually by a forge operator or by an automatic rotation PATENT
• An automatic a-b-c rotation system may include, but is not limited to including, free-swinging clamp-style manipulator tooling or the like to enable a non-limiting thermally managed high strain rate multi-axis forging embodiment disclosed herein.
• an aspect of a thermal management system 33 comprises heating (step 54) an outer surface region 36 of the workpiece 24 to a temperature at or near the workpiece forging temperature. In this manner, the temperature of the workpiece 24 is maintained in a uniform or near uniform and substantially isothermal condition at or near the workpiece forging temperature prior to each high strain rate MAF hit.
• the thermal management system 33 when using the thermal management system 33 to heat the outer surface region 36, together with allowing the adiabatically heated internal region to cool for a specified internal region cooling time, the temperature of the workpiece returns to a substantially uniform temperature at or near the workpiece forging temperature between each a-b-c forging hits.
• the temperature of the workpiece when using the thermal management system 33 to heat the outer surface region 36, together with allowing the adiabatically heated internal region to cool for a specified internal region cooling holding time, the temperature of the workpiece returns to a substantially uniform temperature within the workpiece forging temperature range prior to each high strain rate MAF hit.
• heating 54 an outer surface region 36 of the workpiece 24 may be accomplished using one or more outer surface heating mechanisms 38 of the thermal management system 33.
• Examples of possible heating mechanisms 38 may include, but are not limited to, flame heaters for flame heating; induction heaters for induction heating; and/or radiant heaters for radiant heating of the workpiece 24.
• a non-limiting embodiment of a surface heating mechanism 38 may comprise a box furnace (not shown).
• Other mechanisms and techniques for heating an outer surface of the workpiece will be apparent to those having ordinary skill upon considering the present disclosure, and such mechanisms and techniques are within the scope of the present disclosure.
• a box furnace may be configured with various heating mechanisms to heat the outer surface of the workpiece one or more of flame heating mechanisms, radiant heating mechanisms, induction heating mechanisms, and/or any other heating mechanism known now or hereafter to a person having ordinary skill in the art.
• the temperature of the outer surface region 36 of the workpiece 24 may be heated 54 and maintained at or near the workpiece forging temperature and within the workpiece forging temperature range using one or more die heaters 40 of a thermal management system 33.
• Die heaters 40 may be used to maintain the dies 40 or the die press forging surfaces 44 of the dies at or near the workpiece forging temperature or at temperatures within the temperature forging range.
• Die heaters 40 may heat the dies 42 or the die press forging surface 44 by any suitable heating mechanism known now or hereinafter by a person skilled in the art, including, but not limited to, flame heating mechanisms, radiant heating
• a die heater 40 may be a component of a box furnace (not shown). While the thermal management system 33 is shown in place and being used during the equilibration and cooling steps 32,52,60 of the multi-axis forging process 26 shown in FIGS, 2(b), (d), and (f), it is recognized that the thermal
• an aspect of an embodiment of multi-axis forging 26 comprises press forging (step 56) the workpiece 24 at the workpiece forging temperature in the direction (C) of a third orthogonal axis 58 of the workpiece 24 using a ram speed and strain rate that are sufficient to adiabatically heat the workpiece 24, or at least adiabatically heat an internal region of the workpiece, and plastically deform the workpiece 24.
• the workpiece 24 is deformed during press forging 56 to a plastic deformation of a 20-50% reduction in height or another dimension.
• the workpiece during press forging (56) the workpiece is plastically deformed to a plastic deformation of a 30% to 40% reduction in height or another dimension.
• the workpiece 24 may be press forged (56) in the direction of the second orthogonal axis 48 to the same spacer height used in the first press forging step (28).
• the internal region (not shown) of the workpiece 24 is adiabatically heated during the press forging step (56) to the same temperatures as in the first press forging step (28).
• the high strain rates used for press forging (56) are in the same strain rate ranges as disclosed for the first press forging step (28).
• the workpiece 24 may be rotated 50 to a different orthogonal axis between successive press forging steps ⁇ e.g., 46,56). As discussed above, this rotation may be referred to as a-b-c rotation. It is understood that by using different forge configurations, it may be possible to rotate the ram on the forge instead of rotating the workpiece 24, or a forge may be equipped with multi-axis rams so that rotation of neither the workpiece nor the forge is required. Therefore, rotating 50 the workpiece 24 may be an optional step. In most current industrial set-ups, however, rotating 50 the workpiece to a different orthogonal axis in between press forging step will be required to complete the multi-axis forging process 26.
• process 20 further comprises allowing (step 60) an adiabatically heated internal region (not shown) of the PATENT
• Internal region cooling times may range, for example, from 5 seconds to 120 seconds, from 10 seconds to 60 seconds, or from 5 seconds up to 5 minutes, and it is recognized by a person skilled in the art that the cooling times are dependent upon the size, shape, and composition of the workpiece 24, as well as the characteristics of the environment surrounding the workpiece.
• an aspect of a thermal management system 33 comprises heating (step 62) an outer surface region 36 of the workpiece 24 to a temperature at or near the workpiece forging temperature.
• the temperature of the workpiece 24 is maintained in a uniform or near uniform and substantially isothermal condition at or near the workpiece forging temperature prior to each high strain rate MAF hit.
• using the thermal management system 33 to heat the outer surface region 36, together with allowing the adiabatically heated internal region to cool for a specified internal region cooling time the temperature of the workpiece returns to a substantially uniform temperature at or near the workpiece forging temperature between each a-b-c forging hit.
• the thermal management system 33 uses the thermal management system 33 to heat the outer surface region 36, together with allowing the adiabatically heated internal region to cool for a specified internal region cooling holding time, the temperature of the workpiece returns to a substantially isothermal condition within the workpiece forging temperature range between each a-b- c forging hit.
• heating 62 an outer surface region 36 of the workpiece 24 may be accomplished using one or more outer surface heating mechanisms 38 of the thermal management system 33.
• Examples of possible heating mechanisms 38 may include, but are not limited to, flame heaters for flame heating; induction heaters for induction heating; and/or radiant heaters for radiant heating of the workpiece 24.
• Other mechanisms and techniques for heating an outer surface of the workpiece will be apparent to those having ordinary skill upon considering the present disclosure, and such mechanisms and techniques are within the scope of the present PATENT
• a non-limiting embodiment of a surface heating mechanism 38 may comprise a box furnace (not shown).
• a box furnace may be configured with various heating mechanisms to heat the outer surface of the workpiece using one or more of flame heating mechanisms, radiant heating mechanisms, induction heating
• the temperature of the outer surface region 36 of the workpiece 24 may be heated 62 and maintained at or near the workpiece forging temperature and within the workpiece forging temperature range using one or more die heaters 40 of a thermal management system 33.
• Die heaters 40 may be used to maintain the dies 40 or the die press forging surfaces 44 of the dies at or near the workpiece forging temperature or at temperatures within the temperature forging range.
• the dies 40 of the thermal management system are heated to a temperature within a range that includes the workpiece forging temperature to 100°F (55.6°C) below the workpiece forging temperature.
• Die heaters 40 may heat the dies 42 or the die press forging surface 44 by any suitable heating mechanism known now or hereinafter by a person skilled in the art, including, but not limited to, flame heating mechanisms, radiant heating mechanisms, conduction heating mechanisms, and/or induction heating mechanisms.
• a die heater 40 may be a component of a box furnace (not shown). While the thermal management system 33 is shown in place and being used during the equilibration steps, 32,52,60 of the multi-axis forging process show in FIGS. 2(b), (d), and (f), it is recognized that the thermal management system 33 may or may not be in place during the press forging steps 28,46,56 depicted in FIGS. 2(a), (c), and (e).
• An aspect of this disclosure includes a non-limiting embodiment wherein one or more of the three orthogonal axis press forging, cooling, and surface heating steps are repeated (i.e., are conducted subsequent to completing an initial sequence of the a-b-c forging, internal region cooling, and outer surface region heating steps) until a true strain of at least 3.5 is achieved in the workpiece.
• the phrase "true strain” is also known to a person skilled in the art as “logarithmic strain”, and also as "effective strain”.
• step (g) i.e., repeating (step 64) one or more of steps (a)-(b), (c)-(d), and (e)-(f) until a true strain of at least 3.5 is achieved in the workpiece.
• repeating 64 comprises repeating one or more of steps (a)-(b), (c)-(d), and (e)-(f) until a true strain of at least 4.7 is achieved in the workpiece.
• step (g) i.e., repeating (step 64) one or more of steps (a)-(b), (c)-(d), and (e)-(f) until a true strain of at least 4.7 is achieved in the workpiece.
• repeating 64 comprises repeating one or more of steps (a)-(b), (c)-(d), and (e)-(f) until a true strain of 5 or greater is achieved, or until a true strain of 10 is achieved in the workpiece.
• steps (a)-(f) shown in FIG. 1 are repeated at least 4 times.
• the internal region of the workpiece comprises an average alpha particle grain size from 4pm to 6 pm.
• the workpiece comprises an average grain size in a center region of the workpiece of 4 pm.
• certain non-limiting embodiments of the methods of this disclosure produce grains that are equiaxed.
• the workpiece-press die interface is lubricated with lubricants known to those of ordinary skill, such as, but not limited to, graphite, glasses, and/or other known solid lubricants.
• the workpiece comprises a titanium alloy selected from the group consisting of alpha titanium alloys, alpha+beta titanium alloys, metastable beta titanium alloys, and beta titanium alloys.
• the workpiece comprises an alpha+beta titanium alloy.
• the workpiece comprises a metastable beta titanium alloy.
• Exemplary titanium alloys that may be processed using embodiments of methods according to the present disclosure include, but are not limited to: alpha+beta titanium alloys, such as, for example, Ti-6AI-4V alloy (UNS Numbers R56400 and R54601 ) and Ti-6AI-2Sn-4Zr-2Mo alloy (UNS Numbers R54620 and R54621 ); near-beta titanium PATENT
• the workpiece comprises a titanium alloy that is selected from ASTM Grades 5, 6,12, 19, 20, 21 , 23, 24, 25, 29, 32, 35, 36, and 38 titanium alloys.
• heating a workpiece to a workpiece forging temperature within an alpha+beta phase field of the titanium or titanium alloy metallic material comprises heating the workpiece to a beta soaking temperature
• the beta soaking temperature is in a temperature range of the beta transus temperature of the titanium or titanium alloy metallic material up to 300°F (1 1 1 °C) above the beta transus temperature of the titanium or titanium alloy metallic material.
• Non-limiting embodiments comprise a beta soaking time from 5 minutes to 24 hours.
• the workpiece may also be plastically deformed at a plastic deformation temperature in the beta phase field of the titanium or titanium alloy metallic material prior to cooling the workpiece to the workpiece forging temperature.
• Plastic deformation of the workpiece may comprise at least one of drawing, upset forging, and high strain rate multi-axis forging the workpiece.
• plastic deformation in the beta phase region comprises upset forging the workpiece to a beta-upset strain in the range of 0.1 - 0.5.
• the plastic deformation temperature is in a temperature range including the beta transus temperature of the titanium or titanium alloy metallic PATENT
• FIG. 4 is a schematic temperature-time thermomechanical process chart for a non-limiting method of plastically deforming the workpiece above the beta transus temperature and directly cooling to the workpiece forging temperature.
• a non-limiting method 100 comprises heating 102 the workpiece to a beta soaking temperature 104 above the beta transus temperature 106 of the titanium or titanium alloy metallic material and holding or "soaking" 108 the workpiece at the beta soaking temperature 104 to form an all beta titanium phase microstructure in the workpiece.
• plastic deformation 1 10 comprises upset forging.
• plastic deformation 1 10 comprises upset forging to a true strain of 0.3.
• plastically deforming 1 10 the workpiece comprises thermally managed high strain rate multi-axis forging (not shown in FIG. 4) at a beta soaking temperature.
• the workpiece is cooled 1 12 to a workpiece forging temperature 1 14 in the alpha+beta phase field of the titanium or titanium alloy metallic material.
• cooling 1 12 comprises air cooling.
• the workpiece is thermally managed high strain rate multi-axis forged 1 14, according to non-limiting embodiments of this disclosure.
• the workpiece is hit or press forged 12 times, i.e., the three orthogonal axes of the workpiece are non-sequentially press forged a total of 4 times each.
• the sequence including steps (a)-(b), (c)-(d), and (e)-(f) is performed 4 times.
• the true strain may equal, for example, approximately 3.7.
• the workpiece is cooled 1 16 to room temperature.
• cooling 1 16 comprises air cooling.
• a non-limiting aspect of this disclosure includes thermally managed high strain rate multi-axis forging at two temperatures in the alpha+beta phase field.
• Attorney Docket No. TAV-2139/2144/2174 is a schematic temperature-time thermomechanical process chart for a non-limiting method that comprises multi-axis forging the titanium alloy workpiece at the first workpiece forging temperature utilizing a non-limiting embodiment of the thermal management feature disclosed hereinabove, followed by cooling to a second workpiece forging temperature in the alpha+beta phase, and multi-axis forging the titanium alloy workpiece at the second workpiece forging temperature utilizing a non-limiting embodiment of the thermal management feature disclosed hereinabove.
• a non-limiting method 130 comprises heating 132 the workpiece to a beta soaking temperature 134 above the beta transus temperature 136 of the alloy and holding or soaking 138 the workpiece at the beta soaking temperature 134 to form an all beta phase microstructure in the titanium or titanium alloy workpiece.
• the workpiece may be plastically deformed 140.
• plastic deformation 140 comprises upset forging.
• plastic deformation 140 comprises upset forging to a strain of 0.3.
• plastically deforming 140 the workpiece comprises thermally managed high stain multi-axis forging (not shown in FIG. 5), at a beta soaking temperature.
• the workpiece is cooled 142 to a first workpiece forging temperature 144 in the alpha+beta phase field of the titanium or titanium alloy metallic material.
• cooling 142 comprises air cooling.
• the workpiece is high strain rate multi-axis forged 146 at the first workpiece forging temperature employing a thermal management system according to non-limiting embodiments disclosed herein.
• the workpiece is hit or press forged at the first workpiece forging temperature12 times with 90° rotation between each hit, i.e., the three orthogonal axes of the workpiece are press forged 4 times each.
• the sequence including steps (a)-(b), (c)-(d), and (e)-(f) is performed 4 times.
• the titanium alloy workpiece is cooled 1 8 to a second workpiece forging PATENT
• the workpiece is high strain rate multi-axis forged 150 at the second workpiece forging temperature employing a thermal management system according to non-limiting embodiments disclosed herein.
• the workpiece is hit or press forged at the second workpiece forging temperature a total of 12 times. It is recognized that the number of hits applied to the titanium alloy workpiece at the first and second workpiece forging temperatures can vary depending upon the desired true strain and desired final grain size, and that the number of hits that is appropriate can be determined without undue experimentation.
• the workpiece is cooled 52 to room temperature.
• cooling 152 comprises air cooling to room temperature.
• the first workpiece forging temperature is in a first workpiece forging temperature range of more than 200°F (1 1 1 .1 °C) below the beta transus temperature of the titanium or titanium alloy metallic material to 500°F (277.8°C) below the beta transus temperature of the titanium or titanium alloy metallic material, i.e., the first workpiece forging temperature Ti is in the range of ⁇ - 200°F > ⁇ ⁇ T p - 500°F.
• the second workpiece forging temperature is in a second workpiece forging temperature range of more than 500°F (277.8°C) below the beta transus temperature of the titanium or titanium alloy metallic material to 700°F (388.9°C) below the beta transus temperature, i.e., the second workpiece forging temperature T 2 is in the range of ⁇ ⁇ - 500°F > T 2 ⁇ ⁇ - 700°F.
• the titanium alloy workpiece comprises Ti-6-4 alloy; the first workpiece temperature is 1500°F (815.6°C); and the second workpiece forging temperature is 1300°F (704.4°C).
• FIG. 6 is a schematic temperature-time thermomechanical process chart of a non-limiting method according to the present disclosure of plastically deforming a workpiece comprising a metallic material selected from titanium and a titanium alloy above the beta transus temperature and cooling the workpiece to the workpiece forging temperature, while simultaneously employing thermally managed high strain rate multi-axis forging on the workpiece according to non-limiting PATENT
• a non-limiting method 160 of using thermally managed high strain rate multi-axis forging for grain refining of titanium or a titanium alloy comprises heating 162 the workpiece to a beta soaking temperature 164 above the beta transus temperature 166 of the titanium or titanium alloy metallic material and holding or soaking 168 the workpiece at the beta soaking temperature 164 to form an all beta phase microstructure in the workpiece. After soaking 168 the workpiece at the beta soaking temperature, the workpiece is plastically deformed 170. In a non-limiting embodiment, plastic deformation 170 may comprise thermally managed high strain rate multi-axis forging.
• the workpiece is repetitively high strain rate multi-axis forged 172 using a thermal management system as disclosed herein as the workpiece cools through the beta transus temperature.
• FIG. 6 shows three intermediate high strain rate multi-axis forging 172 steps, but it will be understood that there can be more or fewer intermediate high strain rate multi-axis forging 172 steps, as desired.
• the intermediate high strain rate multi-axis forging 172 steps are intermediate to the initial high strain rate multi-axis forging step 170 at the soaking temperature, and the final high strain rate multi-axis forging step in the alpha+beta phase field 174 of the metallic material. While FIG.
• FIG 6 shows one final high strain rate multi-axis forging step wherein the temperature of the workpiece remains entirely in the alpha+beta phase field, it is understood that more than one multi-axis forging step could be performed in the alpha+beta phase field for further grain refinement. According to non-limiting embodiments of this disclosure, at least one final high strain rate multi-axis forging step takes place entirely at temperatures in the alpha+beta phase field of the titanium or titanium alloy workpiece.
• the multi-axis forging steps 170, 172, 174 take place as the temperature of the workpiece cools through the beta transus temperature of the titanium or titanium alloy metallic material
• a method embodiment such as is shown in FIG. 6 is referred to herein as "through beta transus high strain rate multi-axis forging".
• the thermal management system (33 of FIG. 2) is used in through beta transus multi-axis forging to maintain the temperature of the workpiece at a uniform or substantially uniform temperature prior to each hit at each through beta transus PATENT
• cooling 176 comprises air cooling.
• Non-limiting embodiments of multi-axis forging using a thermal management system can be used to process titanium and titanium alloy workpieces having cross sections greater than 4 square inches using conventional forging press equipment, and the size of cubic workpieces can be scaled to match the capabilities of an individual press. It has been determined that alpha lamellae from the ⁇ -annealed structure break down easily to fine uniform alpha grains at workpiece forging temperatures disclosed in non-limiting embodiments herein. It has also been determined that decreasing the workpiece forging temperature decreases the alpha particle size (grain size).
• grain refinement that occurs in non-limiting embodiments of thermally managed, high strain rate multi-axis forging according to this disclosure occurs via meta-dynamic recrystallization.
• dynamic recrystallization occurs instantaneously during the application of strain to the material.
• meta- dynamic recrystallization occurs at the end of each deformation or forging hit, while at least the internal region of the workpiece is hot from adiabatic heating. Residual adiabatic heat, internal region cooling times, and external surface region heating influence the extent of grain refinement in non-limiting methods of thermally managed, high strain rate multi-axis forging according to this disclosure.
• Multi-axis forging using a thermal management system and cube- shaped workpieces comprising a metallic material selected from titanium and titanium alloys, as disclosed hereinabove has been observed to produce certain less than optimal results. It is believed that one or more of (1 ) the cubic workpiece geometry used in certain embodiments of thermally managed multi-axis forging disclosed herein, (2) die chill ⁇ i.e., letting the temperature of the dies dip significantly below the workpiece PATENT
• An aspect of the present disclosure comprises forging methods that can achieve generally uniform fine grain, very fine grain or ultrafine grain size in billet-size titanium alloys.
• a workpiece processed by such methods may include the desired grain size, such as ultrafine grain microstructure throughout the workpiece, rather than only in a central region of the workpiece.
• Non-limiting embodiments of such methods use "multiple upset and draw” steps on billets having cross-sections greater than 4 square inches. The multiple upset and draw steps are aimed at achieving uniform fine grain, very fine grain or ultrafine grain size throughout the workpiece, while preserving substantially the original dimensions of the workpiece. Because these forging methods include multiple upset and draw steps, they are referred to herein as embodiments of the "MUD" method.
• the MUD method includes severe plastic deformation and can produce uniform ultrafine grains in billet size titanium alloy workpieces.
• strain rates used for the upset forging and draw forging steps of the MUD process are in the range of 0.001 s "1 to 0.02 s "1 , inclusive.
• strain rates typically used for conventional open die upset and draw forging are in the range of 0.03 s "1 to 0.1 s '1 .
• the strain rate for MUD is slow enough to prevent adiabatic heating in order to keep the forging temperature in control, yet the strain rate is acceptable for commercial practices.
• a non-limiting method 200 for refining grains in a workpiece comprising a metallic material selected from titanium and a titanium alloy using multiple upset and draw forging steps comprises heating 202 a cylinder-like titanium or titanium alloy metallic material workpiece to a workpiece forging temperature in the alpha+beta phase field of the metallic material.
• the shape of the cylinder-like workpiece is a cylinder.
• the shape of the cylinder-like workpiece is an octagonal cylinder or a right octagon.
• the cylinder-like workpiece has a starting cross-sectional dimension.
• the starting cross-sectional dimension is the diameter of the cylinder.
• the starting cross-sectional dimension is the diameter of the circumscribed circle of the octagonal cross-section, i.e., the diameter of the circle that passes through all the vertices of the octagonal cross-section.
• the workpiece is upset forged 204.
• the workpiece is rotated (206) 90° and then is subjected to multiple pass draw forging 208.
• Actual rotation 206 of the workpiece is optional, and the objective of the step is to dispose the workpiece into the correct orientation (refer to FIG. 7) relative to a forging device for subsequent multiple pass draw forging 208 steps.
• Multiple pass draw forging comprises incrementally rotating (depicted by arrow 210) the workpiece in a rotational direction (indicated by the direction of arrow 210), followed by draw forging 212 the workpiece after each increment of rotation.
• incrementally rotating and draw forging is repeated 214 until the workpiece comprises the starting cross-sectional dimension.
• the upset forging and multiple pass draw forging steps are repeated until a true strain of at least 3.5 is achieved in the workpiece.
• embodiment comprises repeating the heating, upset forging, and multiple pass draw forging steps until a true strain of at least 4.7 is achieved in the workpiece.
• the heating, upset forging, and multiple pass draw forging steps are repeated until a true strain of at least 10 is achieved in the workpiece. It is observed in non-limiting embodiments that when a true strain of 10 imparted to the MUD forging, a UFG alpha microstructure is produced, and that increasing the true strain imparted to the workpiece results smaller average grain sizes.
• An aspect of this disclosure is to employ a strain rate during the upset and multiple drawing steps that is sufficient to result in severe plastic deformation of the PATENT
• a strain rate used in upset forging is in the range of 0.001 s "1 to 0.003 s "1 .
• a strain rate used in the multiple draw forging steps is the range of 0.01 s "1 to 0.02 s "1 . It is determined that strain rates in these ranges do not result in adiabatic heating of the workpiece, which enables workpiece temperature control, and are sufficient for an economically acceptable commercial practice.
• the workpiece after completion of the MUD method, has substantially the original dimensions of the starting cylinder 214 or octagonal cylinder 216. In yet another non-limiting embodiment, after completion of the MUD method, the workpiece has substantially the same cross-section as the starting workpiece. In a non-limiting embodiment, a single upset requires many draw hits to return the workpiece to a shape including the starting cross-section of the workpiece.
• incrementally rotating and draw forging further comprises multiples steps of rotating the cylindrical workpiece in 15° increments and subsequently draw forging, until the cylindrical workpiece is rotated through 360° and is draw forged at each increment.
• incremental rotation + draw forging steps are employed to bring the workpiece to substantially its starting cross-sectional dimension.
• incrementally rotating and draw forging further comprises multiples steps of rotating the cylindrical workpiece in 45° increments and subsequently draw forging, until the cylindrical workpiece is rotated through 360° and is draw forged at each increment.
• eight incremental rotation + draw forging steps are employed to bring the workpiece substantially to its starting cross-sectional dimension. It was observed in non-limiting embodiments of the MUD method that manipulation of an octagonal cylinder by handling equipment was more precise than manipulation of a cylinder by PATENT
• a workpiece forging temperature comprises a temperature within a workpiece forging temperature range.
• the workpiece forging temperature is in a workpiece forging temperature range of 100°F (55.6°C) below the beta transus temperature (T p ) of the titanium or titanium alloy metallic material to 700°F (388.9°C) below the beta transus temperature of the titanium or titanium alloy metallic material.
• the workpiece forging temperature is in a temperature range of 300°F (166.7°C) below the beta transition temperature of the titanium or titanium alloy metallic material to 625°F (347°C) below the beta transition temperature of the titanium or titanium alloy metallic material.
• the low end of a workpiece forging temperature range is a temperature in the alpha+beta phase field at which substantial damage does not occur to the surface of the workpiece during the forging hit, as may be determined without undue
• the workpiece forging temperature range for a Ti-6-4 alloy (Ti-6AI-4V; UNS No.
• R56400 which has a beta transus temperature (T p ) of about 1850°F (1010°C), may be, for example, from 1 150°F (621 .1°C) to 1750°F (954.4°C), or in another embodiment may be from 1225 ⁇ (662.8°C) to 1550°F (843.3°C).
• Non-limiting embodiments comprise multiple reheating steps during the MUD method.
• the titanium alloy workpiece is heated to the workpiece forging temperature after upset forging the titanium alloy workpiece.
• the titanium alloy workpiece is heated to the workpiece forging temperature prior to a draw forging step of the multiple pass draw forging.
• the workpiece is heated as needed to bring the actual workpiece temperature back to the workpiece forging temperature after an upset or draw forging step.
• embodiments of the MUD method impart redundant work or extreme deformation, also referred to as severe plastic deformation, which is aimed at creating ultrafine grains in a workpiece comprising a metallic material selected from titanium and a titanium alloy.
• severe plastic deformation which is aimed at creating ultrafine grains in a workpiece comprising a metallic material selected from titanium and a titanium alloy.
• the temperature of the workpiece may be cooled 216 to a second workpiece forging temperature.
• the workpiece is upset forged at the second workpiece forging temperature 218.
• the workpiece is rotated 220 or oriented for subsequent draw forging steps.
• the workpiece is multiple- step draw forged at the second workpiece forging temperature 222.
• Multiple-step draw forging at the second workpiece forging temperature 222 comprises incrementally rotating 224 the workpiece in a rotational direction (refer to FIG. 7), and draw forging at the second workpiece forging temperature 226 after each increment of rotation.
• the steps of upset, incrementally rotating 224, and draw forging are repeated 226 until the workpiece comprises the starting cross-sectional dimension.
• the steps of upset forging at the PATENT are repeated 226 until the workpiece comprises the starting cross-sectional dimension.
• the workpiece forging temperature is about 1600°F (871 .1 °C) and the second workpiece forging temperature is about 1500°F (815.6°C).
• Subsequent workpiece forging temperatures that are lower than the first and second workpiece forging temperatures such as a third workpiece forging temperature, a fourth workpiece forging temperature, and so forth, are within the scope of non-limiting embodiments of this disclosure.
• grain refinement results in decreasing flow stress at a fixed temperature. It was determined that decreasing the forging temperature for sequential upset and draw steps keeps the flow stress constant and increases the rate of microstructural refinement. It has been determined that in non-limiting embodiments of MUD according to this disclosure, a true strain of 10 results in a uniform equiaxed alpha ultrafine grain microstructure in titanium and titanium alloy workpieces, and that the lower temperature of a two-temperature (or multi-temperature) MUD process can be determinative of the final grain size after a true strain of 10 is imparted to the MUD forging.
• An aspect of this disclosure includes that after processing by the MUD method, subsequent deformation steps are possible without coarsening the refined grain size, as long as the temperature of the workpiece is not subsequently heated above the beta transus temperature of the titanium alloy.
• a subsequent deformation practice after MUD processing may include draw forging, multiple draw forging, upset forging, or any combination of two or more of these forging steps at temperatures in the alpha+beta phase field of the titanium or titanium alloy.
• subsequent deformation or forging steps include a combination of multiple pass draw forging, upset forging, and draw forging to reduce the starting cross-sectional dimension of the cylinder-like workpiece to a fraction PATENT
• the workpiece comprises a titanium alloy selected from the group consisting of an alpha titanium alloy, an alpha+beta titanium alloy, a metastable beta titanium alloy, and a beta titanium alloy.
• the workpiece comprises an alpha+beta titanium alloy.
• the workpiece comprises a metastable beta titanium alloy.
• the workpiece is a titanium alloy selected from ASTM Grades 5, 6,12, 19, 20, 21 , 23, 24, 25, 29, 32, 35, 36, and 38 titanium alloys.
• the workpiece Prior to heating the workpiece to the workpiece forging temperature in the alpha+beta phase field according to MUD embodiments of this disclosure, in a non- limiting embodiment the workpiece may be heated to a beta soaking temperature, held at the beta soaking temperature for a beta soaking time sufficient to form a 100% beta phase titanium microstructure in the workpiece, and cooled to room temperature.
• the beta soaking temperature is in a beta soaking temperature range that includes the beta transus temperature of the titanium or titanium alloy up to 300°F (1 1 1 °C) above the beta transus temperature of the titanium or titanium alloy.
• the beta soaking time is from 5 minutes to 24 hours.
• the workpiece is a billet that is coated on all or certain surfaces with a lubricating coating that reduces friction between the workpiece and the forging dies.
• the lubricating coating is a solid lubricant such as, but not limited to, one of graphite and a glass lubricant.
• Other lubricating coatings known now or hereafter to a person having ordinary skill in the art are within the scope of this disclosure.
• the contact area between the workpiece and the forging dies is small relative to the contact area in multi-axis forging of a cubic PATENT
• the workpiece Prior to heating the workpiece comprising a metallic material selected from titanium and titanium alloys to the workpiece forging temperature in the alpha+beta phase field according to MUD embodiments of this disclosure, in a non-limiting embodiment, the workpiece is plastically deformed at a plastic deformation temperature in the beta phase field of the titanium or titanium alloy metallic material after being held at a beta soaking time sufficient to form 100% beta phase in the titanium or titanium alloy and prior to cooling to room temperature. In a non-limiting embodiment, the plastic deformation temperature is equivalent to the beta soaking temperature. In another non- limiting embodiment, the plastic deformation temperature is in a plastic deformation temperature range that includes the beta transus temperature of the titanium or titanium alloy up to 300°F (1 1 1°C) above the beta transus temperature of the titanium or titanium alloy.
• plastically deforming the in the beta phase field of the titanium or titanium alloy comprises at least one of drawing, upset forging, and high strain rate multi-axis forging the titanium alloy workpiece.
• plastically deforming the workpiece in the beta phase field of the titanium or titanium alloy comprises multiple upset and draw forging according to non-limiting embodiments of this disclosure, and wherein cooling the workpiece to the workpiece forging temperature comprises air cooling.
• plastically deforming the workpiece in the beta phase field of the titanium or titanium alloy comprises upset forging the workpiece to a 30-35% reduction in height or another dimension, such as length.
• Another aspect of this disclosure may include heating the forging dies during forging.
• a non-limiting embodiment comprises heating dies of a forge used to forge the workpiece to temperature in a temperature range bounded by the workpiece forging temperature to 100°F (55.6°C) below the workpiece forging temperature, inclusive.
• a non-limiting embodiment of the method comprises heating a workpiece comprising a metal or a metal alloy to a workpiece forging temperature. After heating, the workpiece is forged at the workpiece forging temperature at a strain rate sufficient to adiabatically heat an internal region of the workpiece. After forging, a waiting period is employed before the next forging step.
• the temperature of the adiabatically heated internal region of the metal alloy workpiece is allowed to cool to the workpiece forging temperature, while at least a one surface region of the workpiece is heated to the workpiece forging temperature.
• the steps of forging the workpiece and then allowing the adiabatically heated internal region of the workpiece to equilibrate to the workpiece forging temperature while heating at least one surface region of the metal alloy workpiece to the workpiece forging temperature are repeated until a desired characteristic is obtained.
• forging comprises one or more of press forging, upset forging, draw forging, and roll forging.
• the metal alloy is selected from the group consisting of titanium alloys, zirconium and zirconium alloys, aluminum alloys, ferrous alloys, and superalloys.
• the desired alloy is selected from the group consisting of titanium alloys, zirconium and zirconium alloys, aluminum alloys, ferrous alloys, and superalloys.
• Mechanical properties include, but are not limited to, strength, ductility, fracture toughness, and hardness,
• Multi-axis forging using a thermal management system was performed on a titanium alloy workpiece consisting of alloy Ti-6-4 having equiaxed alpha grains with grain sizes in the range of 10-30 pm.
• a thermal management system was PATENT
• the beta annealed workpiece was then heated in a gas-fired box furnace to the workpiece forging temperature of 1500°F (815.6°C), which is in the alpha+beta phase field of the alloy.
• the beta annealed workpiece was first press forged in the direction of the A axis of the workpiece to a spacer height of 3.25 inches.
• the ram speed of the press forge was 1 inch/second, which corresponded to a strain rate of 0.27 s "1 .
• the adiabatically heated center of the workpiece and the flame heated surface region of the workpiece were allowed to equilibrate to the workpiece forging temperature for about 4.8 minutes.
• the workpiece was rotated and press forged in the direction of the B axis of the workpiece to a spacer height of 3.25 inches.
• the ram speed of the press forge was 1 inch/second, which corresponded to a strain rate of 0.27 s "1 .
• the adiabatically heated center of the workpiece and the flame heated surface region of the workpiece were allowed to equilibrate to the workpiece forging
• FIG. 10 is a micrograph of the beta annealed material of Example 1 showing equiaxed grains with grain sizes between 1 0-30 pm.
• FIG. 1 1 is a micrograph of a center region of the a-b-c forged sample of Example 1 .
• the grain structure of FIG. 1 1 has equiaxed grain sizes on the order of 4 pm and would qualify as "very fine grain” (VFG) material.
• VFG very fine grain
• Finite element modeling was used to determine internal region cooling times required to cool the adiabatically heated internal region to a workpiece forging temperature.
• a 5 inch diameter by 7 inch long alpha-beta titanium alloy preform was virtually heated to a multi-axis forging temperature of 1500°F (815.6°C).
• the forging dies were simulated to be heated to 600°F (315.6°C).
• a ram speed was simulated at 1 inch/second, which corresponds to a strain rate 0.27 s "1 .
• Different intervals for the internal region cooling times were input to determine an internal region cooling time required to cool the adiabatically heated internal region of the simulated workpiece to the workpiece forging temperature. From the plot of FIG. 10, it is seen that the modeling suggests that internal region cooling times of between 30 and 45 seconds could be used to cool the adiabatically heated internal region to a workpiece forging temperature of about 1500°F (815.6°C).
• High strain rate multi-axis forging using a thermal management system was performed on a titanium alloy workpiece consisting of a 4 inch (10.16 cm) sided cube of alloy Ti-6-4.
• the titanium alloy workpiece was beta annealed at 1940°F
• the titanium alloy workpiece was heated to a workpiece forging temperature of 1500°F (815.6°C), which is in the alpha-beta phase field of the titanium alloy workpiece.
• the workpiece was multi-axis forged using a thermal management system comprising gas flame heaters and heated dies according to non-limiting embodiments of this disclosure to equilibrate the temperature of the external surface region of the workpiece to the workpiece forging temperature between the hits of multi- axis forging.
• the workpiece was press forged to 3.2 inches (8.13 cm). Using a-b-c rotation, the workpiece was subsequently press forged in each hit to 4 inches
• a ram speed of 1 inch per second (2.54 cm/s) was used in the press forging steps, and a pause, i.e., an internal region cooling time or equilibration time of 15 seconds was used between press forging hits.
• the equilibration time is the time that is allowed for the adiabatically heated internal region to cool to the workpiece forging temperature while heating the external surface region to the workpiece forging temperature.
• a total of 12 hits were used at the 1500°F (815.6°C) workpiece
• the cubic workpiece was a-b-c forged four times.
• the temperature of the workpiece was then lowered to a second workpiece forging temperature of 1300°F (704.4°C).
• the titanium alloy workpiece was high strain multi-axis forged according to non-limiting embodiments of this disclosure, using a ram speed of 1 inch per second (2.54 cm/s) and internal region cooling times of 15 seconds between each forging hit.
• the same thermal management system used to manage the first workpiece forging temperature was used to manage the second workpiece forging temperature.
• a total of 6 forging hits were applied at the second workpiece forging temperature, i.e., the cubic workpiece was a-b-c forged two times at the second workpiece forging temperature.
• FIG. 13 A micrograph of the center of the cube after processing as described in Example 4 is shown in FIG. 13. From FIG. 13, it is observed that the grains at the center of the cube have an equiaxed average grain size of less than 3 pm, i.e., an ultrafine grain size.
• Finite element modeling was used to simulate deformation in thermally managed multi-axis forging of a cube.
• the simulation was carried out for a 4 inch sided cube of Ti-6-4 alloy that was beta annealed at 1940°F (1060°C) until an all beta microstructure is obtained.
• the simulation used isothermal multi-axis forging, as used in certain non-limiting embodiments of a method disclosed herein, conducted at 1500°F (815.6°C).
• the workpiece was a-b-c press forged with twelve total hits, i.e., four sets of a-b-c orthogonal axis forgings/rotations.
• the cube was cooled to 1300°F (704.4°C) and high strain rate press forged for 6 hits, i.e., two sets of a-b-c orthogonal axis forgings/rotations.
• the simulated ram speed was 1 inch per second (2.54 cm/s).
• the results shown in FIG. 15 predict levels of strain in the cube after processing as described above.
• the finite element modeling simulation predicts a maximum strain of 16.8 at the center of the cube. The highest strain, however, is very localized, and the majority of the cross-section does not achieve a strain greater than 10.
• a workpiece comprising alloy Ti-6-4 in the configuration of a five-inch diameter cylinder that is 7 inches high ⁇ i.e., measured along the longitudinal axis) was beta annealed at 1940°F (1060°C) for 60 minutes.
• the beta annealed cylinder was air quenched to preserve the all beta microstructure.
• the beta annealed cylinder was heated to a workpiece forging temperature of 1500°F (815.6°C) and was followed by multiple upset and draw forging according to non-limiting embodiments of this
• the multiple upset and draw sequence included upset forging to a 5.25 inch height (i.e., reduced in dimension along the longitudinal axis), and multiple draw forging, PATENT
• FIG. 16(a) A micrograph of a center region of a cross-section of the sample prepared in Example 7 is presented in FIG. 16(a).
• FIG. 16(b) A micrograph of the near surface region of a cross-section of the sample prepared in Example 7 is presented in FIG. 16(b).
• FIGS. 16(a) and (b) Examination of FIGS. 16(a) and (b) reveals that the sample processed according to Example 7 achieved a uniform and equiaxed grain structure having an average grain size of less than 3 pm, which is classified as very fine grain (VFG).
• VFG very fine grain
• a workpiece comprising alloy Ti-6-4 configured as a ten-inch diameter cylindrical billet having a length of 24 inches was coated with silica glass slurry lubricant.
• the billet was beta annealed at 1940°C.
• the beta annealed billet was upset forged from 24 inches to a 30-35% reduction in length.
• the billet was subjected to multiple pass draw forging, which comprised incrementally rotating and draw forging the billet to a ten-inch octagonal cylinder.
• the beta processed octagonal cylinder was air cooled to room temperature.
• the octagonal cylinder was heated to a first workpiece forging temperature of 1600°F (87 .1°C).
• the octagonal cylinder was upset forged to a 20-30% reduction in length, and then multiple draw forged, which included rotating the working by 45° increments followed by draw forging, until the octagonal cylinder achieved its starting cross-sectional dimension. Upset forging and multiple pass draw forging at the first workpiece forging temperature was repeated three times, and the workpiece was reheated as needed to bring the workpiece temperature back to the workpiece forging temperature. The workpiece was cooled to a second workpiece forging temperature of1500°F (815.6°F). The multiple upset and draw forging procedure used at the first workpiece forging temperature was repeated at the second workpiece forging PATENT
• the workpiece was multiple pass draw forged at a temperature in the alpha+beta phase field using conventional forging parameters and cut in half for upset.
• the workpiece was upset forged at a temperature in the alpha+beta phase field using conventional forging parameters to a 20% reduction in length.
• the workpiece was draw forged to a 5 inch diameter round cylinder having a length of 36 inches.
• FIG. 18 A macro-photograph of a cross-section of a sample processed according to the non-limiting embodiment of Example 9 is presented in FIG. 18. It is seen that a uniform grain size is present throughout the billet.
• FIG. 19 A micrograph of the sample processed according to the non-limiting embodiment of Example 9 is presented in Figure 19. The micrograph demonstrates that the grain size is in the very fine grain size range.
• Finite element modeling was used to simulate deformation of the sample prepared in Example 9. The finite element model is presented in FIG. 20. The finite element model predicts relatively uniform effective strain of greater than 10 for the majority of the 5-inch round billet.

Priority Applications (14)

Applications Claiming Priority (2)

Publications (1)

Family

ID=44545948

Family Applications (1)

Country Status (20)

Cited By (2)

Families Citing this family (58)

Citations (2)

Family Cites Families (385)

• 2010
  • 2010-09-15 US US12/882,538 patent/US8613818B2/en active Active
• 2011
  • 2011-08-22 DK DK14191903.5T patent/DK2848708T3/en active
  • 2011-08-22 WO PCT/US2011/048546 patent/WO2012036841A1/en active Application Filing
  • 2011-08-22 UA UAA201304579A patent/UA113149C2/uk unknown
  • 2011-08-22 EP EP14191903.5A patent/EP2848708B1/en active Active
  • 2011-08-22 PT PT141919035T patent/PT2848708T/pt unknown
  • 2011-08-22 KR KR1020137005622A patent/KR101835908B1/ko active IP Right Grant
  • 2011-08-22 EP EP11752026.2A patent/EP2616563B1/en active Active
  • 2011-08-22 MX MX2013002595A patent/MX2013002595A/es active IP Right Grant
  • 2011-08-22 HU HUE11752026A patent/HUE031577T2/en unknown
  • 2011-08-22 PL PL14191903T patent/PL2848708T3/pl unknown
  • 2011-08-22 CN CN201610976215.6A patent/CN106834801B/zh active Active
  • 2011-08-22 RU RU2013116806/02A patent/RU2581331C2/ru not_active IP Right Cessation
  • 2011-08-22 AU AU2011302567A patent/AU2011302567B2/en not_active Ceased
  • 2011-08-22 CA CA2810388A patent/CA2810388C/en not_active Expired - Fee Related
  • 2011-08-22 PL PL11752026T patent/PL2616563T3/pl unknown
  • 2011-08-22 BR BR112013005795A patent/BR112013005795B1/pt not_active IP Right Cessation
  • 2011-08-22 PT PT117520262T patent/PT2616563T/pt unknown
  • 2011-08-22 DK DK11752026.2T patent/DK2616563T3/en active
  • 2011-08-22 CN CN201180044613.XA patent/CN103189530B/zh not_active Expired - Fee Related
  • 2011-08-22 ES ES14191903.5T patent/ES2652295T3/es active Active
  • 2011-08-22 HU HUE14191903A patent/HUE037427T2/hu unknown
  • 2011-08-22 NO NO14191903A patent/NO2848708T3/no unknown
  • 2011-08-22 ES ES11752026.2T patent/ES2611856T3/es active Active
  • 2011-08-22 CA CA3013617A patent/CA3013617C/en not_active Expired - Fee Related
  • 2011-08-22 JP JP2013529162A patent/JP6109738B2/ja active Active
  • 2011-08-26 TW TW105105766A patent/TWI591194B/zh not_active IP Right Cessation
  • 2011-08-26 TW TW100130790A patent/TWI529256B/zh active
• 2013
  • 2013-03-05 IL IL225059A patent/IL225059A/en active IP Right Grant
  • 2013-09-17 US US14/028,588 patent/US10435775B2/en active Active
• 2015
  • 2015-12-17 AU AU2015271901A patent/AU2015271901B2/en not_active Ceased

Patent Citations (2)

Non-Patent Citations (5)

Also Published As

Similar Documents

Legal Events